Glass composition and glass substrate

ABSTRACT

A glass substrate for use as the substrate of an information recording medium such as a magnetic disk, magneto-optical disk, DVD, or MD or of an optical communication device, and a glass composition for making such a glass substrate, contains the following glass ingredients: 45 to 75% by weight of SiO 2 ; 1 to 20% by weight of Al 2 O 3 ; 0 to 15% by weight, zero inclusive, of B 2 O 3 ; SiO 2 +Al 2 O 3 +B 2 O 3  accounting for 65 to 90% by weight; a total of 7 to 20% by weight of R 2 O compounds, where R=Li, Na, and K; and a total of 0 to 12% by weight, zero inclusive, of R′O compounds, where R′=Mg, Ca, Sr, Ba, and Zn. Moreover, the following conditions are fulfilled: B 2 O 3 =0% by weight, or Al 2 O 3 /B 2 O 3 ≧1.0; and (SiO 2 +Al 2 O 3 +B 2 O 3 )/(the total of R 2 O compounds+the total of R 2 O compounds)≧3.

This application is based on the following Japanese Patent Applications, the contents of which are hereby incorporated by reference.

Japanese Patent Application No. 2002-283059 filed on Sep. 27, 2002

Japanese Patent Application No. 2003-071789 filed on Mar. 17, 2003

BACKGROUND OF THE INVENTION

1. Field of the Invention

The present invention relates to a glass substrate and to a glass composition for making a glass substrate. More particularly, the present invention relates to a glass substrate for use as a substrate of an information recording medium such as a magnetic disk, magneto-optical disk, DVD, or MD or of an optical communication device, and to a glass composition for making such a glass substrate.

2. Description of the Prior Art

Conventionally, magnetic disks for use in stationary devices such as desk-top computers and servers typically have substrates made of aluminum alloy, and those for use in portable devices such as notebook computers and mobile computers typically have substrates made of glass. However, aluminum alloy is prone to deformation, and is not hard enough to offer satisfactory surface smoothness on the surfaces of a substrate after polishing. Moreover, when a head makes mechanical contact with a magnetic disk, the magnetic film is liable to exfoliate from the substrate. For these reasons, substrates made of glass, which offer satisfactory surface smoothness and high mechanical strength, are expected to be increasingly used in the future not only in portable devices but also in stationary devices and other home-use information devices.

One known type of glass substrate is those made of chemically strengthened glass, in which the alkali elements present near the surface of the substrate are replaced with other alkali elements in order to produce compression strain and thereby increase mechanical strength. However, chemically strengthened glass requires a complicated ion exchange process, and does not permit reprocessing once ion exchange is complete. This makes it difficult to achieve a high yield rate. Moreover, to permit ion exchange to take place in the glass substrate, alkali ions need to be left easily movable therein. Thus, the alkali ions that are present near the surface of the substrate may move to the surface and exude therefrom during the heating step when the magnetic film is formed, or erode the magnetic film, or degrade the bond strength of the magnetic film.

Another type of glass substrate, known as common glass substrates that are not treated by chemical strengthening, is those made of soda lime. However, soda lime is not mechanically strong or chemically durable enough to be suitable as a material for substrates for information recording. Glass materials used in substrates of liquid crystal panels or the like are so prepared as to have a low or no alkali content so that they have low linear thermal expansion coefficients. This helps maintain thermal stability at high temperatures. However, as a result, these materials have linear thermal expansion coefficients that greatly differ from that of, for example, stainless steel (SUS), of which clamps and spindle motor components are made. This often causes trouble when a recording medium is mounted in a recording device or when information is recorded. Moreover, these materials are not mechanically strong enough to be suitable as a material for substrates for information recording.

Glass substrates are used also as substrates in optical communication devices such as optical filters and optical switches. These devices, however, are occasionally degraded by elution of the alkali content from their glass substrate. Moreover, the higher the density of the film formed on a glass substrate, the more the wavelength shifts ascribable to variations in temperature and humidity can be reduced. There is a limit, however, to the density of a film that can be formed by vapor deposition, which is the method widely used conventionally.

Furthermore, in a case where a glass substrate is used for information recording, when an information recording film is formed on the glass substrate, the pressure, heat, or impact applied to its surface may produce a crack in the glass substrate, leading to a lower product yield.

SUMMARY OF THE INVENTION

An object of the present invention is to provide a glass substrate, and a glass composition for making it, that has high mechanical strength without being treated by strengthening, that has low alkali elution, that has a linear thermal expansion coefficient close to that of motor components, that has a high fracture toughness, and that has a predetermined surface hardness.

To achieve the above object, according to the present invention, a glass substrate, and a glass composition for making it, contains the following glass ingredients: 45 to 75% by weight of SiO₂; 1 to 20% by weight of Al₂O₃; 0 to 15% by weight, zero inclusive, of B₂O₃; SiO₂+Al₂O₃+B₂O₃ accounting for 65 to 90% by weight; a total of 7 to 20% by weight of R₂O compounds, where R=Li, Na, and K; and a total of 0 to 12% by weight, zero inclusive, of R′O compounds, where R′=Mg, Ca, Sr, Ba, and Zn. Moreover, the following conditions are fulfilled: B₂O₃=0% by weight, or Al₂O₃/B₂O₃≧1.0; and (SiO₂+Al₂O₃+B₂O₃)/(the total of R₂O compounds+the total of R′O compounds)≧3. It is to be noted that, in the following descriptions, “%” denotes “percent by weight” unless otherwise stated. The glass composition described above has high rigidity without being subjected to strengthening, has an adequate surface hardness to prevent scratches on its surface but permit easy surface treatment such as polishing, and has low alkali elution. Moreover, as compared with conventional glass compositions, the glass composition described above has a higher linear thermal expansion coefficient, which is thus closer to that of hard disk drive components. This makes trouble unlikely when a recording medium is mounted in a recording device or when information is recorded. Moreover, the glass composition described above has a high fracture toughness. This prevents breakage of a substrate as when a substrate for information recording is fabricated.

BRIEF DESCRIPTION OF THE DRAWINGS

This and other objects and features of the present invention will become clear from the following description, taken in conjunction with the preferred embodiments with reference to the accompanying drawings in which:

FIG. 1 is a perspective view showing an example of an information recording medium employing a glass substrate according to the invention; and

FIG. 2 is a diagram schematically showing a pressure mark and cracks produced when a pressure is applied to the surface of a glass substrate with a Vickers indenter.

DESCRIPTION OF THE PREFERRED EMBODIMENTS

The inventors of the present invention have made an intensive study in search of a way of increasing the rigidity of a glass substrate without treating it by strengthening, increasing the linear thermal expansion coefficient thereof than ever while reducing the alkali elution therefrom, enhancing the chemical durability thereof, and increasing the fracture toughness thereof The study has led the inventors to find out that it is possible to obtain predetermined rigidity by using SiO₂ as the matrix ingredient of glass and adding thereto predetermined amounts of Al₂O₃ and B₂O₃ to form the skeleton of glass, that it is possible to obtain a higher fracture toughness by controlling within a predetermined range the ratio of the total content of the skeleton ingredients of glass to the total content of R₂O (where R represents Li, Na, and K) and R′O (where R′ represents Mg, Ca, Sr, Ba, and Zn), and that it is possible to obtain a higher linear thermal expansion coefficient while achieving lower alkali elution by controlling within a predetermined range the total content of particular alkali metal oxides. These findings have led to the present invention.

Hereinafter, the grounds for setting limitations on the ingredients of a glass composition according to the present invention will be explained. First of all, SiO₂ is an ingredient that forms the matrix of glass. With a SiO₂ content less than 45%, the glass has an unstable structure. This not only degrades the chemical durability of the glass, but also degrades the melt viscosity properties thereof, making the glass difficult to mold. On the other hand, with a SiO₂ content higher than 75%, the glass shows low fusibility. This lowers productivity and makes it impossible to obtain sufficient rigidity. Hence, a preferred range of the SiO₂ content is from 45 to 75%. A further preferred range is from 50 to 72%.

Al₂O₃ gets into the matrix of glass, and serves to stabilize the structure of the glass and enhance the chemical durability thereof. With an Al₂O₃ content lower than 1%, the glass structure is not stabilized sufficiently. On the other hand, with an Al₂O₃ content higher than 20%, the glass shows low fusibility, lowering productivity. Hence, a preferred range of the Al₂O₃ content is from 1 to 20%. A further preferred range is from 3 to 16%.

B₂O₃ improves the fusibility of glass and thereby enhances productivity. In addition, it gets into the matrix of the glass, and serves to stabilize the structure of the glass and enhance the chemical durability thereof With a B₂O₃ content higher than 15%, the glass shows poor melt viscosity properties. This makes the glass difficult to mold, and makes the glass unstable. Hence, a preferred range of the B203 content is 15% or lower (zero inclusive). A further preferred upper limit is 12%, and a preferred lower limit is 0.5%.

If the total content of these three glass ingredients, which are the skeletal ingredients of glass, is less than 65%, the glass has a brittle structure. On the other hand, if their total content is higher than 90%, the glass shows low fusibility, lowering productivity. Hence, a preferred total content of those glass ingredients is from 65 to 90%. A further preferred range is from 68 to 88%.

Alkali metal oxides R₂O (R=Li, Na, and K) improve the fusibility of glass, and increase the linear thermal expansion coefficient thereof. With a total alkali metal oxide content lower than 7%, the fusibility is not improved sufficiently, nor is the linear thermal expansion coefficient increased sufficiently. On the other hand, with a total alkali metal oxide content higher than 20%, excess amounts of alkali metal oxides are dispersed throughout the skeleton of the glass, increasing alkali elution. Hence, a preferred range of the total alkali metal oxide content is from 7 to 20%. A further preferred range is 8 to 18%. Moreover, to obtain a so-called mixed alkali effect, which helps reduce alkali elution, it is preferable that the lower limit of the content of each alkali metal oxide be 0.1%. On the other hand, for satisfactory chemical durability and melt stability, it is preferable that the upper limit of the Li₂O and Na₂O contents be 15% each and that of the K₂O content be 10%.

Divalent metal oxides R′O (R′=Mg, Ca, Sr, Ba, and Zn) increase the rigidity of glass, improve the fusibility thereof, and stabilize the structure thereof. With a total R′O content higher than 12%, the glass has an unstable structure, leading to lower melt productivity and lower chemical durability. Hence, a preferred R′O content is 12% or lower. A further preferred upper limit of the total R′O content is 10%. Preferred contents of the individual R′O ingredients are given below.

MgO increases the rigidity of glass and improves the fusibility thereof. With a MgO content higher than 10%, the glass may have an unstable structure, lowering the melt productivity and chemical durability of the glass. Hence, a preferred range of the MgO content is from 0 to 10%. A further preferred upper limit is 8%.

CaO increases the linear thermal expansion coefficient and rigidity of glass, and improves the fusibility thereof With a CaO content higher than 10%, the glass may have an unstable structure, lowering the melt productivity and chemical durability of the glass. Hence, a preferred range of the MgO content is from 0 to 10%. A further preferred upper limit is 8%.

SrO increases the linear thermal expansion coefficient of glass, stabilizes the structure thereof, and improves the fusibility thereof With a SrO content higher than 8%, the glass may have an unstable structure. Hence, a preferred range of the SrO content is from 0 to 8%. A further preferred upper limit is 6%.

BaO exerts the same effects as SrO. With a BaO content higher than 8%, the glass may have an unstable structure. Hence, a preferred range of the BaO content is from 0 to 8%. A further preferred upper limit is 6%.

ZnO increases the chemical durability and rigidity of glass, and improves the fusibility thereof. With a ZnO content higher than 6%, the glass may have an unstable structure, lowering the melt productivity and chemical durability of the glass. Hence, a preferred range of the ZnO content is from 0 to 6%. A further preferred upper limit is 5%.

In a glass composition according to the invention, when the B₂O₃ content is not zero, the ratio of the Al₂O₃ content to the B₂O₃ content needs to be 1.0 or higher. With the Al₂O₃/B₂O₃ ratio lower than 1.0, the skeleton of glass contains an excess amount of B₂O₃, giving the glass a brittle structure.

In addition, the ratio of the total content of SiO₂+Al₂O₃+B₂O₃ to the total content of all R₂O ingredients+all R′O ingredients needs to be 3 or higher. With the (SiO₂+Al₂O₃+B₂O₃)/(all R₂O ingredients+all R′O ingredients) ratio lower than 3, the glass contains an excess amount of R₂O and R′O ingredients, which are modification oxides, relative to its skeletal ingredients, and thus has an unstable structure. A further preferred lower limit of this ratio is 3.5, and a preferred upper limit is 12.

A glass composition according to the invention may further contain, as necessary, predetermined amounts of one or more of the glass ingredients TiO₂, ZrO₂, and Ln_(x)O_(y). However, with a total content of TiO₂+ZrO₂+Ln_(x)O_(y) higher than 15%, the glass may be unstable, with greatly reduced toughness and a higher tendency to devitrification, leading to extremely low productivity. Hence, a preferred range of the total content of these glass ingredients is from 0 to 15%. A further preferred range of their total content is from 0.5 to 12%. Preferred contents of those individual glass ingredients are given below.

TiO₂ strengthens the structure of glass, enhances the rigidity thereof, and improves the fusibility thereof. With a TiO₂ content higher than 10%, the glass may have an unstable structure, lowering the melt productivity and chemical durability of the glass. Hence, a preferred range of the TiO₂ content is from 0 to 10%. A further preferred range is from 0.5 to 8%.

ZrO₂ strengthens the structure of glass, enhances the rigidity thereof, and enhances the chemical durability thereof With a ZrO₂ content higher than 10%, the glass shows low fusibility, making it impossible to enhance productivity. Hence, a preferred range of the ZrO₂ content is from 0 to 10%. A further preferred range is 0.5 to 8%.

Ln_(x)O_(y) strengthens the structure of glass, and enhances the rigidity thereof. With a Ln_(x)O_(y) content higher than 8%, the glass has an unstable structure, leading to lower melt productivity and a high specific gravity. This makes the glass unsuitable for use as a hard disk drive component. Hence, a preferred Ln_(x)O_(y) content is 8% or lower. A further preferred upper limit is 6%. Here, Ln_(x)O_(y) represents at least one compound selected from the group consisting of lanthanoid metal oxides, Y₂O₃, Nb₂O₅, and Ta₂O₅. Lanthanoid metal oxides include different types of compounds of composition Ln₂O₃, LnO, and the like, and examples of Ln include La, Ce, Er, Pr, Nd, Pm, Sm Eu, Gd, Tb, Dy, Ho, Tm, Yb, and Lu.

To a glass composition according to the invention, 2% or less of a clarifier such as Sb₂O₃ may also be added. As required, any other conventionally known glass ingredient or additive may be added so long as it does not spoil the effects achieved by the present invention.

In a glass composition according to the invention, it is preferable that the glass transition temperature Tg be 600° C. or lower, that, for satisfactory productivity in the melt molding step and out of other considerations, the liquid phase temperature T_(L) be 1 300° C. or lower, and that the temperature T_(logη=2) at which the glass composition has a melt viscosity of log η=2 be 1 550° C. or lower. The glass transition temperature, the liquid phase temperature, and T_(logη=2) can be controlled within these ranges in the following manner. For example, the glass transition temperature is controlled by adjusting, so long as the desired main properties are not degraded, the total content and proportions of the skeletal ingredients SiO₂, B₂O₃, and Al₂O₃ and the content of alkali metal oxides, i.e., the ingredients that greatly reduce the glass transition temperature. The liquid phase temperature can be controlled by adjusting the total content and proportions of ingredients of which the addition in excess amounts makes the glass unstable. T_(logη=2) can be controlled by adjusting, so long as the desired main properties are not degraded, the proportions in which SiO₂, i.e., the main ingredient that increases the viscosity, and other ingredients that improve the viscosity are added.

Next, a glass substrate according to the present invention will be described. The main feature of a glass substrate according to the invention is that it is formed of a glass composition as described above. A glass substrate according to the invention is produced by any conventionally known fabrication process, for example in the following manner. Raw materials of glass ingredients, i.e., oxides, carbonates, nitrates, hydroxides, and the like corresponding to the individual ingredients, are, in the desired proportions and in the form of powder, fully mixed to obtain a blending of the raw materials. This blending is then put, for example, in a platinum crucible placed inside an electric furnace heated to 1 300 to 1 550° C., where the blending is first melted and clarified and then stirred and homogenized. The molten glass is then poured into a preheated mold, and is cooled slowly so as to be formed into a glass block. Next, the glass block is heated again to close to its glass transition point and is then cooled slowly so as to be straightened. The glass block thus obtained is then sliced into a disk, and is cut out using a core drill so as to have concentric outer and inner edges. Alternatively, the molten glass is formed into a disk by press molding. The disk-shaped glass material thus obtained is then formed into a glass substrate by subjecting the two flat surfaces of the glass material to coarse and fine polishing and then to cleaning using at least one of a water liquid, an acidic liquid, or an alkaline liquid.

In a case where a glass substrate according to the invention is used, for example, as a substrate of an information recording medium, to minimize the floating distance of the head and the film thickness of the recording medium, it is preferable that the glass substrate have, after the polishing step, a surface roughness Ra of 1 nm or lower and, after the cleaning step, a surface roughness Ra′ equal to or lower than 1.5 times the surface roughness Ra. With a glass substrate containing alkali ingredients in high proportions and treated by strengthening, it is possible to obtain a surface roughness Ra of 1 nm or lower by polishing, but, when the surface of the substrate is cleaned with water, an acid, or an alkali in the following cleaning step, owing to its low chemical durability, its surface is violently eroded, resulting in a high surface roughness Ra′ after the cleaning step. On the other hand, with a glass substrate that is not treated by strengthening, its composition is uniform between at the surface and in the interior, and therefore, in general, the surface roughness Ra′ of the substrate does not change so much during the cleaning step. Accordingly, by optimizing the glass ingredients, it is possible to control the surface roughness Ra′ after the cleaning step within 1.5 times the surface roughness Ra after the polishing step.

It is preferable that a glass substrate according to the invention have properties that fulfill the following conditions. First, it is preferable that a glass substrate according to the invention have a specific elastic modulus E/ρ of 31 or higher. With a glass substrate that is not treated by strengthening, its mechanical strength depends on its rigidity. Thus, with a specific elastic modulus lower than 31, the substrate has insufficient mechanical strength so that, when it receives impact while being mounted in a hard disk drive, it is prone to breakage at where it is fastened to a hard disk drive member. A further preferred specific elastic modulus E/ρ is 32 or higher.

It is preferable that a glass substrate according to the invention have a Vickers hardness Hv in the range of from 500 to 700. With a Vickers hardness lower than 500, the substrate is prone to breakage resulting from impact and to damage in the fabrication process. On the other hand, a Vickers hardness higher than 700 lowers the rate at which the glass substrate can be polished in the polishing step, makes it difficult to obtain a surface with the desired flatness, and makes it difficult to adjust the surface shape of the substrate by tape texture polishing, or correct surface defects by scrub washing, or perform other treatment. The Vickers hardness of the substrate can be controlled within that range, for example, by adjusting, so long as the desired main properties are not degraded, the proportions of the ingredients in such a way as to increase the ion fill factor. A further preferred lower limit of the Vickers hardness Hv is 520, and a further preferred upper limit thereof is 680.

It is preferable that a glass substrate according to the invention have alkali elution A of 350 ppb or lower per 2.5-inch disk. With alkali elution A higher than 350 ppb, when the glass substrate is used in an information recording medium, the recording film such as a magnetic film that is formed on the surface of the glass substrate is degraded by elution of the alkali ingredients from the substrate. Further preferable alkali elution A is 320 ppb or lower.

It is preferable that a glass substrate according to the invention have a linear thermal expansion coefficient α in the range of from 60×10⁻⁷ to 90×10⁻⁷/° C. With a linear thermal expansion coefficient α outside this range, when an information recording medium is produced using the glass substrate, its linear thermal expansion coefficient differs so greatly from that of the material of the drive unit in which the information recording medium is mounted as to produce stress around where the information recording medium is mounted. As a result, the substrate may break or deform, causing deviations in recording positions and thus making reading and writing of data impossible. A further preferred lower limit of the linear thermal expansion coefficient is 62×10⁻⁷/° C., and a further preferred higher limit thereof is 88×10⁻⁷/° C.

It is preferable that a glass substrate according to the invention have a fracture toughness Kc higher than 0.80. With a fracture toughness Kc of 0.80 or lower, when the glass substrate is used in an information recording medium, a crack may develop in the glass substrate when pressure or the like is applied thereto in the step of forming a recording film such as a magnetic film on the surface thereof. Moreover, with a fracture toughness Kc of 0.80 or lower, the substrate is prone to damage when it is machined, leading to a low machining yield. A further preferred lower limit of the fracture toughness Kc is 0.85.

It is preferable that a glass substrate according to the invention, when melted and kept at 1 500° C. for 24 hours, exhibit a weight reduction factor lower than 8.0%. A weight reduction factor of 8.0% or higher leads to unstable properties and lower productivity.

In a glass substrate according to the invention, as described earlier, it is preferable that the glass transition temperature Tg be 600° C. or lower, that, for satisfactory productivity in the melt molding step and out of other considerations, the liquid phase temperature T_(L) be 1 300° C. or lower, and that the temperature T_(logη=2) at which the glass substrate has a melt viscosity of log η=2 be 1 550° C. or lower. The glass transition temperature, the liquid phase temperature, and T_(logη=2) can be controlled within these ranges in the following manner. For example, the glass transition temperature is controlled by adjusting, so long as the desired main properties are not degraded, the total content and proportions of the skeletal ingredients SiO₂, B₂O₃, and Al₂O₃ and the content of alkali metal oxides, i.e., the ingredients that greatly reduce the glass transition temperature. The liquid phase temperature can be controlled by adjusting the total content and proportions of ingredients of which the addition in excess amounts makes the glass unstable. T_(logη=2) can be controlled by adjusting, so long as the desired main properties are not degraded, the proportions in which SiO₂, i.e., the main ingredient that increases the viscosity, and other ingredients that improve the viscosity are added.

A glass substrate according to the invention can be used to produce disks of any diameter, for example 3.5-inch, 2.5-inch, 1.8-inch, and any smaller-diameter disks, with any thickness, for example 2 mm thick, 1 mm thick, 0.63 mm thick, and any slimmer disks.

Next, an information recording medium employing a glass substrate according to the present invention will be described. When employed as a substrate of an information recording medium, a glass substrate according to the invention contributes to durability and high recording density. Now, such an information recording medium will be described with reference to the drawing.

FIG. 1 is a perspective view of a magnetic disk. This magnetic disk D is composed of a circular glass substrate 1 and a magnetic film 2 formed directly on a surface thereof The magnetic film 2 may be formed by any conventionally known method. For example, it is formed by spin-coating the substrate with a thermosetting resin having magnetic particles dispersed therein, or by sputtering, or by electroless plating. Spin-coating provides a film thickness of about 0.3 to 1.2 μm, sputtering provides a film thickness of about 0.04 to 0.08 μm, and electroless plating provides a film thickness of about 0.05 to 0.1 μm. To minimize the film thickness and maximize the density, it is preferable to form the magnetic film 2 by sputtering or electroless plating.

The magnetic film may be formed out of any conventionally known magnetic material, of which a preferred example is a Co-based alloy that contains Co, which exhibits high crystal anisotropy, as its main ingredient so as to have high coercivity and that has Ni and Cr added thereto to adjust remanent magnetic flux density. Specifically, examples of such alloys containing Co as their main ingredient include CoPt, CoCr, CoNi, CoNiCr, CoCrTa, CoPtCr, CoNiPt, CoNiCrPt, CoNiCrTa, CoCrPtTa, CoCrPtB, and CoCrPtSiO. The magnetic film may be divided into a plurality of layers with one or more non-magnetic films (for example, Cr, CrMo, or CrV) laid in between so as to form a multilayer structure (for example, CoPtCr/CrMo/CoPtCr or CoCrPtTa/CrMo/CoCrPtTa) with a view to reducing noise. Instead of the magnetic materials mentioned above, it is also possible to use a magnetic material of a granular type having magnetic particles of Fe, Co, FeCo, CoNiPt, or the like dispersed in a non-magnetic film of a ferrite-based material, an iron/rare earth-based material, SiO₂, BN, or the like. The magnetic film may be for either surface recording or vertical recording.

To ensure smooth sliding of a magnetic head, the magnetic film may be coated with a thin layer of lubricant on the surface. An example of the lubricant is perfluoro polyether (PFPE), a liquid lubricant, diluted with a CFC-based solvent.

As required, a primer or protective layer may additionally be formed. In a magnetic disk, the material of the primer layer is selected according to the magnetic film. The primer layer is formed out of, for example, one or more selected from non-magnetic metals such as Cr, Mo, Ta, Ti, W, V, B, Al, and Ni. With a magnetic film containing Co as its main ingredient, Cr used singly or a Cr alloy is preferred for better magnetic properties and out of other considerations. The primer layer may be composed of a single layer, or may be composed of a plurality of layers of identical or different types laid over one another to form a multilayer primer layer such as Cr/Cr, Cr/CrMo, Cr/CrV, NiAl/Cr, NiAl/CrMo, or NiAl/CrV.

The protective layer for preventing wear and corrosion of the magnetic film may be a layer of Cr, Cr alloy, carbon, hydrogenated carbon, zirconia, silica, or the like. Such a protective layer can be formed in continuous steps with the primer layer, the magnetic film, and the like using an in-line-type sputtering machine. The protective layer may be composed of a single layer, or may be composed of a plurality of layers of identical or different types laid over one another to form a multilayer protective layer. It is also possible to form, on top of or instead of the protective layer described above, another protective layer. For example, instead of the protective layer described above, a layer of silicon oxide (SiO₂) may be formed by applying, on top of a Cr layer, and then burning fine particles of colloidal silica dispersed in tetraalkoxysilane diluted with an alcohol-based solvent.

A magnetic disk has been described above as an example of an information recording medium according to the invention. It is to be understood, however, that a glass substrate according to the invention applies not only to this type of information recording medium but also to magneto-optical disks, optical disks, and the like.

Moreover, a glass substrate according to the invention is suitably used also in optical communication devices. A glass substrate according to the invention has alkali elution as low as 350 ppb or lower per 2.5-inch disk, and therefore the film formed thereon is not degraded by elution of the alkali ingredients therefrom. Moreover, compared with conventional glass substrates, a glass substrate according to the invention has a linear thermal expansion coefficient as high as from 60×10⁻⁷/° C. to 90×10⁻⁷/° C., and therefore, when the glass substrate heated in the vapor deposition step is cooled, it shrinks more, compressing the film formed on the surface thereof more and thereby increasing the density of the film. This helps alleviate the wavelength shifts resulting from variations in temperature and humidity.

Now, an optical filter for dense wavelength division multiplexing (DWDM) will be described as an example of an optical communication device employing a glass substrate according to the present invention. An optical filter employing a dielectric multilayer film has high-refractive-index layers and low-refractive-index layers laid over one another. These layers are formed by any conventionally known method, examples of which include vacuum deposition, sputtering, ion plating, and ion beam assisted deposition. Among these methods, vacuum deposition is preferred for the high productivity it provides. Vapor deposition is a method of forming a thin film by heating a material to be evaporated in a vacuum and making the resulting vapor condense on and adhere to a base substrate. The material to be evaporated is heated by one of various methods such as by resistance heating, in an externally heated crucible, with an electron beam, with microwaves, or with a laser beam. Specifically, the material is evaporated in a vacuum of about 1×10⁻³ to 5×10⁻³ Pa. While the material is being evaporated, the amount of oxygen introduced is adjusted by controlling a solenoid valve so that the degree of vacuum is kept constant. The thickness of each film so formed is monitored so that evaporation is stopped when the desired film thickness is obtained.

There is no particular restriction on the thickness of individual films, but each film is routinely given a thickness equal to one-fourth of the wavelength, generally up to 1 μm. The total number of films generally exceeds 100. The films are formed out of, for example, a dielectric, semiconductor, or metal, among which a dielectric is particularly preferred.

An optical filter for DWDM has been described above as an example of an optical communication device employing a glass substrate according to the invention. It is to be understood, however, that a glass substrate according to the invention applies not only to this type of optical communication device but also to other types of optical communication device such as optical switches and multiplexing/branching devices.

EXAMPLES Practical Examples 1 to 233 and Comparative Examples 1 to 5

For each of different glass compositions, which each correspond to one of Practical Examples 1 to 233 and Comparative Examples 1 to 5, prescribed amounts of glass ingredients in the form of powder were weighed and put in a platinum crucible, were mixed, and then were melted at 1 550° C. in an electric furnace. When the ingredients were melted sufficiently, stirring blades were put into the molten glass to stir it for about one hour. Thereafter, the stirring blades were taken out, then the molten glass was allowed to stand for 30 minutes, and then it was poured into a mold so as to be formed into a glass block. The glass block was then heated again to close to its glass transition point, and was then cooled slowly so as to be straightened. The glass block thus obtained was then sliced into a disk about 1.5 mm thick and 2.5 inches across, and was cut out using a cutter so as to have concentric inner and outer edges. The two flat surfaces of this disk were subjected to coarse and fine polishing and then to cleaning to obtain a glass substrate of the corresponding Practical or Comparative Example. With each of the glass substrates thus produced, its properties were evaluated in the manners described below. The composition of the glass substrate of each example and the results obtained therewith are shown in Tables 1 to 12.

Specific Elastic Modulus

First the Young's modulus E was measured by the method for testing dynamic modulus of elasticity included in the methods for testing elasticity of fine ceramics defined in JIS (Japanese Industrial Standards) R 1602, and then it was divided by the specific gravity measured by the balance method to calculate the specific elastic modulus.

Vickers Hardness Hv

The Vickers hardness Hv was measured using a Vickers hardness tester under the following conditions: with a load of 100 g, and with loading duration of 15 seconds.

Alkali Elution A

The alkali elution A was determined by first polishing the surface of the glass substrate with cerium oxide so as to obtain a smooth surface having an Ra value of 2 nm or lower, then cleaning the surface, then immersing the glass substrate in 50 ml of reverse osmosis membrane water at 80° C. for 24 hours, and then analyzing the elution liquid with an ICP emission spectrocherical analyzer.

Linear Thermal Expansion Coefficient α

The linear thermal expansion coefficient α was measured using a differential dilatometer under the following conditions: with a load of 5 g, within a temperature range of from 25 to 100° C., and at a temperature increase rate of 5° C./min.

Fracture Toughness Kc

The fracture toughness Kc was determined using a Vickers hardness tester and according to the formula noted below on the basis of the pressure mark produced with a Vickers indenter under the following conditions: with a load of 500 g, and with loading duration of 15 seconds. Kc=0.018(E/Hv)^(1/2)(P/C ^(3/2))=0.026E ^(1/2) P ^(1/2) a/C ^(3/2) where Kc represents the fracture toughness (Pa·m^(1/2)), E represents the elastic modulus (Pa), Hv represents the Vickers hardness (Pa), P represents the pressing load (N), C represents half the average of the lengths of cracks (m), and “a” represents half the average of the lengths of the diagonals of the pressure mark (m).

Glass Transition Point Tg

The glass transition point Tg was measured using a differential thermal analyzer while the glass sample prepared in the form of powder was heated within a temperature range of from room temperature to 900° C. at a temperature increase rate of 10° C./min.

Liquid Phase Temperature T_(L)

The liquid phase temperature T_(L) was determined by first keeping the glass sample in a molten state at 1 550° C. for 2 hours, then keeping it at 1 300° C. for 10 hours, then cooling it rapidly, and then checking for devitrification at the surface or in the interior of the glass sample. A glass sample is evaluated as “OK” if no devitrification was observed therewith and as “NG” if devitrification was observed therewith.

Temperature T_(logη=2)

The viscosity of the molten glass was measured using a stirring viscosity tester, and the temperature T_(logη=2) at which log η=2 was determined. A glass composition is evaluated as “OK” if T_(logη=2) was 1 550° C. or lower and as “NG” if T_(logη=2) was higher than 1 550° C.

Weight Reduction Factor

The weight reduction factor was determined according to the formula noted below by melting 50 g of glass cullets in a platinum crucible, keeping it at 1 500° C. for 24 hours, and measuring its weight before and after the application of heat thereto. Weight Reduction Factor (%)=(Weight Before−Weight After)/Weight Before×100

Tables 1 to 12 show the following. The glass substrates of Practical Examples 1 to 233 had specific elastic moduli of 32 or higher, i.e., higher than with conventional glass substrates, and had adequate Vickers hardnesses in the range of from 530 to 680, i.e., adequate surface hardnesses. Moreover, they had alkali elution of 350 ppb or lower, i.e., lower than with conventional glass substrates. Furthermore, they had linear thermal expansion coefficients in the range of from 60×10⁻⁷ to 90×10⁻⁷/° C., i.e., close to those of hard disk drive components. Moreover, they all had facture toughnesses of 0.80 or higher, i.e., practically acceptable facture toughnesses. Moreover, they exhibited satisfactory glass fusibility.

On the other hand, Table 6 shows the following. The glass substrate of Comparative Example 1, of which the SiO₂ content was as low as 43.1%, had a weak glass structure and high alkali elution. Moreover, this glass substrate, having a high total content of R′O (R=Mg, Ca, and Zn) and thus having a low content of skeletal ingredients (SiO₂+Al₂O₃+B₂O₃) relative to the total content of R₂O and R′O ingredients, had a low Vickers hardness and a low facture toughness. Moreover, this glass substrate suffered devitrification. The glass substrate of Comparative Example 2, of which the SiO₂ content was as high as 76.8%, had a low specific elastic modulus and a high T_(logη=2) value, and exhibited poor glass fusibility. The glass substrate of Comparative Example 3, having a low (SiO₂+Al₂O₃+B₂O₃) content, having a high R₂O (R=Li, Na, and K) content, and having a low content of skeletal ingredients (SiO₂+Al₂O₃+B₂O₃) relative to the total content of R₂O and R′O ingredients, was unsatisfactory in all of its specific elastic modulus, Vickers hardness, alkali elution, linear thermal expansion coefficient, and fracture toughness.

Table 12 shows the following. The glass substrate of Comparative Example 4, of which the B₂O₃ content was as high as 15.7%, had a weak glass structure, high alkali elution, and a high weight reduction factor. This glass substrate also had a low linear thermal expansion coefficient. The glass substrate of Comparative Example 5, of which the Al₂O₃/B₂O₃ ratio was as low as 0.53, had a weak glass structure, and, like the glass substrate of Comparative Example 4, had high alkali elution and a high weight reduction factor. Moreover, this glass substrate had a low fracture toughness and a high T_(logη=2) value, and exhibited poor glass fusibility.

TABLE 1 Practical Example Glass Composition (% by Weight) 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 SiO₂ 56.2 59.2 53.1 53.5 63.5 59.3 58.7 59.9 62.8 56.1 56.1 61.1 60.5 59.9 58.8 56.1 56.1 54.0 55.0 58.1 Al₂O₃ 15.8 7.3 12.5 10.1 4.7 5.9 5.9 6.0 6.3 5.6 5.6 5.6 5.6 5.5 5.4 8.6 11.6 14.2 12.2 5.6 B₂O₃ 5.0 5.0 3.7 3.3 4.1 4.1 4.2 4.4 3.9 3.9 3.9 3.9 3.8 3.8 3.9 3.9 3.6 3.6 3.9 Li₂O 3.4 3.4 4.1 3.9 3.4 4.3 4.2 4.3 4.5 4.1 4.1 5.2 5.1 5.1 5.0 4.1 4.1 3.7 3.7 4.1 Na₂O 3.8 3.8 4.5 4.3 3.7 4.7 4.7 4.8 5.0 4.5 4.5 5.7 5.7 5.6 5.5 4.5 4.5 4.1 4.1 4.5 K₂O 1.9 1.9 2.3 2.1 1.9 2.4 2.4 2.4 2.5 2.3 2.3 2.9 2.9 2.8 2.8 2.3 2.3 2.0 2.0 2.3 MgO 8.7 4.4 4.3 4.1 3.6 2.3 4.6 2.3 2.3 0.5 1.0 1.9 6.3 2.3 5.9 5.9 7.3 CaO 4.4 6.3 6.0 5.2 3.3 6.6 3.3 3.3 0.5 1.0 1.9 1.3 2.3 0.7 1.7 1.3 SrO BaO ZnO 3.0 5.0 2.5 2.5 2.5 2.4 TiO₂ 3.1 3.6 3.5 3.3 2.9 3.7 3.7 3.7 3.9 3.5 3.5 3.5 3.5 3.4 3.4 3.5 3.5 3.2 3.2 3.5 ZrO₂ 0.5 5.5 4.4 4.2 3.6 4.6 4.6 4.7 4.9 4.4 4.4 4.4 4.3 4.3 4.2 4.4 4.4 4.0 4.0 4.4 La₂O₃ 1.4 1.4 4.9 4.6 4.1 5.1 5.1 5.2 5.4 6.9 4.9 4.9 4.8 4.8 4.7 4.9 4.9 4.4 4.4 4.9 CeO₂ Er₂O₃ Gd₂O₃ Y₂O₃ Nb₂O₅ Ta₂O₅ Sb₂O₃ 0.3 0.3 0.3 0.3 0.2 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 SiO₂ + Al₂O₃ + B₂O₃ 76.9 71.4 65.7 67.3 71.4 69.3 68.6 70.1 73.4 65.7 65.7 70.7 70.0 69.3 67.9 68.7 71.7 71.8 70.8 67.7 R₂O:Li₂O + Na₂O + 9.2 9.2 10.8 10.3 9.0 11.4 11.3 11.5 12.0 10.8 10.8 13.8 13.6 13.5 13.3 10.8 10.8 9.8 9.8 10.8 K₂O R′O:MgO + CaO + 8.7 8.7 10.5 10.0 8.8 5.6 6.6 4.6 0.0 8.5 10.5 2.5 3.5 4.5 6.3 7.5 4.5 6.6 7.6 8.5 SrO + BaO + ZnO Al₂O₃/B₂O₃ 3.15 1.45 — 2.71 1.43 1.43 1.43 1.43 1.43 1.43 1.43 1.43 1.43 1.43 1.43 2.20 2.97 3.99 3.43 1.43 (SiO₂ + Al₂O₃ + B₂O₃)/ 4.31 4.00 3.08 3.32 4.02 4.09 3.85 4.37 6.10 3.40 3.08 4.33 4.08 3.86 3.48 3.75 4.68 4.38 4.07 3.50 (R₂O + R′O) TiO₂ + ZrO₂ + LnxOy 5.0 10.5 12.7 12.1 10.6 13.4 13.3 13.6 14.2 14.7 12.7 12.7 12.6 12.5 12.2 12.7 12.7 11.6 11.6 12.7 Specific Elastic Modulus 34.0 34.0 34.1 33.9 33.4 33.8 33.4 33.3 32.8 32.7 32.7 32.5 33.2 32.7 33.8 33.6 33.1 33.4 33.7 33.7 (E/ρ) Expansion Coefficient 64 64 74 72 66 67 71 66 66 69 68 72 71 74 78 70 66 65 65 68 α(×10⁻⁷/° C.) Vickers Hardness Hv 591 621 677 662 666 653 650 642 634 668 657 616 660 650 630 662 645 616 652 656 Fracture Toughness Kc 0.96 0.83 0.88 0.83 0.90 0.87 0.82 0.87 1.00 0.84 0.87 0.93 1.05 0.88 0.86 0.90 1.02 1.13 1.02 0.94 Alkali Elution A(ppb) 181 190 239 224 189 203 210 192 251 224 239 213 219 226 238 310 198 344 323 228 Tg 560 547 567 540 546 527 530 528 529 524 528 501 526 527 527 535 534 521 522 529 T_(L) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ T_(logη=2) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯

TABLE 2 Practical Example Glass Composition (% by Weight) 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 SiO₂ 55.5 55.5 55.5 55.5 55.5 55.5 54.5 53.4 50.4 54.5 61.1 57.3 61.1 61.1 61.1 57.0 56.4 54.8 56.1 53.4 Al₂O₃ 8.5 8.5 8.5 11.5 11.5 11.5 12.1 11.1 13.2 8.4 5.6 8.8 5.6 5.6 5.6 8.5 11.1 11.3 11.6 11.1 B₂O₃ 3.9 3.9 3.9 3.9 3.9 3.9 3.5 7.5 9.0 5.7 3.9 4.0 3.9 3.9 3.9 3.9 7.5 7.7 7.9 7.5 Li₂O 4.4 4.4 4.4 4.4 4.4 4.4 4.0 4.2 3.8 4.3 5.2 4.5 5.2 5.2 5.2 4.4 4.2 4.0 3.7 3.4 Na₂O 4.9 4.9 4.9 4.9 4.9 4.9 4.4 4.7 4.2 4.8 5.7 5.0 5.7 5.7 5.7 4.9 4.7 4.4 4.1 6.2 K₂O 2.4 2.4 2.4 2.4 2.4 2.4 2.2 2.4 2.1 2.4 2.9 2.5 2.9 5.4 2.9 2.4 2.4 2.2 2.1 1.7 MgO 6.2 6.2 6.2 2.2 2.2 2.2 5.8 2.2 5.5 6.1 1.0 6.4 2.0 2.0 2.0 6.2 2.2 2.0 1.9 2.2 CaO 1.3 2.2 2.2 2.2 1.7 2.2 0.7 1.2 1.0 1.3 2.0 2.0 2.0 1.3 2.2 2.0 1.9 2.2 SrO 1.3 BaO 1.3 ZnO 2.5 2.5 2.5 TiO₂ 3.5 3.5 3.5 3.5 3.5 3.5 3.2 3.3 3.0 3.4 3.5 3.6 3.5 3.5 4.4 5.0 3.3 3.1 2.9 3.3 ZrO₂ 4.3 4.3 4.3 4.3 4.3 4.3 3.9 4.2 3.7 4.2 4.4 4.4 4.4 4.4 4.4 4.3 4.2 3.9 3.6 4.2 La₂O₃ 4.8 4.8 4.8 4.8 4.4 4.6 4.1 4.7 2.9 1.9 0.9 0.9 1.8 1.6 4.3 4.1 4.6 CeO₂ Er₂O₃ Gd₂O₃ Y₂O₃ Nb₂O₅ 4.8 Ta₂O₅ 4.8 Sb₂O₃ 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.2 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.2 0.3 SiO₂ + Al₂O₃ + B₂O₃ 67.9 67.9 67.9 70.9 70.9 70.9 70.1 72.0 72.7 68.5 70.7 70.0 70.7 70.7 70.7 69.4 75.0 73.9 75.5 72.0 R₂O:Li₂O + Na₂O + 11.7 11.7 11.7 11.7 11.7 11.7 10.7 11.3 10.1 11.5 13.8 12.1 13.8 16.3 13.8 11.7 11.3 10.5 9.9 11.3 K₂O R′O:MgO + CaO + 7.5 7.5 7.5 4.5 4.5 4.5 7.5 4.3 6.1 7.3 4.5 7.7 6.5 4.0 6.5 7.5 4.3 4.0 3.8 4.3 SrO + BaO + ZnO Al₂O₃/B₂O₃ 2.20 2.20 2.20 2.97 2.97 2.97 3.43 1.47 1.46 1.46 1.43 2.20 1.43 1.43 1.43 2.20 1.47 1.47 1.47 1.47 (SiO₂ + Al₂O₃ + B₂O₃)/ 3.54 3.54 3.54 4.37 4.37 4.37 3.86 4.62 4.49 3.64 3.86 3.54 3.48 3.48 3.48 3.62 4.81 5.08 5.54 4.62 (R₂O + R′O) TiO₂ + ZrO₂ + LnxOy 12.6 12.6 12.6 12.6 12.6 12.6 11.5 12.1 10.8 12.4 10.7 9.9 8.7 8.7 8.8 11.1 9.1 11.3 10.6 12.1 Specific Elastic Modulus 33.7 33.4 32.6 33.2 33.2 33.2 33.8 32.7 33.0 34.0 33.4 34.0 33.6 33.2 34.0 34.1 33.3 33.4 33.3 33.5 (E/ρ) Expansion Coefficient 70 72 76 69 71 70 68 73 65 68 78 71 79 86 77 70 65 62 62 66 α(×10⁻⁷/° C.) Vickers Hardness Hv 644 633 639 626 633 632 663 640 642 636 616 628 618 598 618 632 608 615 611 623 Fracture Toughness Kc 0.93 0.91 0.90 0.94 0.95 0.92 0.98 0.92 1.09 0.87 0.88 0.87 0.88 0.85 0.88 0.87 0.94 0.94 0.97 0.92 Alkali Elution A(PPb) 270 288 278 225 211 226 259 189 183 219 228 227 242 334 188 222 184 173 161 189 Tg 530 525 522 530 528 531 522 522 517 527 519 517 513 492 522 522 509 517 513 522 T_(L) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ T_(logη=2) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯

TABLE 3 Practical Example Glass Composition (% by Weight) 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60 SiO₂ 71.8 66.8 66.8 66.8 66.8 66.8 69.1 69.1 62.5 62.5 66.8 66.8 66.8 66.8 66.8 66.8 62.5 64.0 69.1 70.6 Al₂O₃ 6.3 9.3 9.3 9.3 9.3 9.3 9.6 9.6 13.9 13.9 11.3 11.3 13.3 13.3 14.6 14.6 15.4 13.9 11.1 9.6 B₂O₃ 3.4 5.4 5.4 5.4 5.4 5.4 2.7 2.7 5.0 5.0 3.4 3.4 1.4 1.4 5.0 5.0 2.7 2.7 Li₂O 4.5 6.0 6.8 9.1 5.6 6.7 6.8 9.1 6.8 9.1 6.8 9.1 6.8 9.1 6.8 9.1 6.0 6.0 6.0 6.0 Na₂O 5.0 5.5 3.5 2.0 3.3 1.7 3.5 2.0 3.5 2.0 3.5 2.0 3.5 2.0 3.5 2.0 5.0 5.0 5.0 5.0 K₂O 2.5 1.8 1.8 1.0 3.1 3.7 1.8 1.0 1.8 1.0 1.8 1.0 1.8 1.0 1.8 1.0 2.5 2.5 2.5 2.5 MgO CaO SrO BaO ZnO TiO₂ 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 ZrO₂ 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 0.6 0.6 0.6 0.6 La₂O₃ 2.4 1.2 2.4 2.4 2.4 2.4 2.4 2.4 2.4 2.4 2.4 2.4 2.4 2.4 2.4 2.4 0.7 0.7 0.7 0.7 CeO₂ Er₂O₃ Gd₂O₃ Y₂O₃ Nb₂O₅ Ta₂O₅ Sb₂O₃ 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 SiO₂ + Al₂O₃ + B₂O₃ 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 82.9 82.9 82.9 82.9 R₂O:Li₂O + Na₂O + 12.0 13.3 12.0 12.0 12.0 12.0 12.0 12.0 12.0 12.0 12.0 12.0 12.0 12.0 12.0 12.0 13.5 13.5 13.5 13.5 K₂O R′O:MgO + CaO + SrO + BaO + ZnO Al₂O₃/B₂O₃ 1.86 1.73 1.73 1.73 1.73 1.73 3.57 3.57 2.77 2.77 3.34 3.34 9.68 9.68 — — 3.07 2.77 4.13 3.57 (SiO₂ + Al₂O₃ + B₂O₃)/ 6.76 6.12 6.76 6.76 6.76 6.76 6.76 6.76 6.76 6.76 6.76 6.76 6.76 6.76 6.76 6.76 6.12 6.12 6.12 6.12 (R₂O + R′O) TiO₂ + ZrO₂ + LnxOy 6.2 5.0 6.2 6.2 6.2 6.2 6.2 6.2 6.2 6.2 6.2 6.2 6.2 6.2 6.2 6.2 3.2 3.2 3.2 3.2 Specific Elastic Modulus 33.3 33.9 33.7 34.6 33.2 33.3 33.5 34.2 33.9 34.6 33.7 34.4 33.5 34.1 33.5 34.2 33.8 33.7 33.4 33.3 (E/ρ) Expansion Coefficient 65 69 65 67 65 64 68 67 66 68 66 68 67 68 67 68 71 71 70 71 α(×10⁻⁷/° C.) Vickers Hardness Hv 609 583 583 570 580 562 574 573 578 582 570 575 574 569 565 557 573 578 559 566 Fracture Toughness Kc 1.11 1.10 1.05 1.11 1.12 1.17 1.11 1.05 1.12 1.02 1.07 1.07 1.24 1.30 1.18 1.04 1.22 1.15 1.24 1.17 Alkali Elution A(ppb) 159 180 178 214 216 171 235 266 131 232 151 207 186 280 199 279 177 158 222 235 Tg 500 501 502 500 506 500 501 497 507 503 513 498 519 508 528 520 501 495 491 489 T_(L) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ T_(logη=2) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯

TABLE 4 Practical Example Glass Composition (% by Weight) 61 62 63 64 65 66 67 68 69 70 71 72 73 74 75 76 77 78 79 80 SiO₂ 62.5 62.5 69.1 69.1 66.8 66.8 62.5 69.1 66.8 66.8 66.8 66.8 66.8 66.8 66.8 66.8 66.8 66.8 56.4 54.8 Al₂O₃ 13.9 13.9 9.6 9.6 11.3 13.3 13.9 9.6 12.3 12.3 12.3 12.3 12.3 12.3 12.3 12.3 12.3 12.3 11.1 11.3 B₂O₃ 5.0 5.0 2.7 2.7 3.4 1.4 5.0 2.7 2.4 2.4 2.4 2.4 2.4 2.4 2.4 2.4 2.4 2.4 7.5 7.7 Li₂O 5.5 6.5 5.5 6.5 6.5 6.5 6.5 6.5 6.8 6.8 6.8 6.8 6.8 6.8 6.8 6.8 6.8 6.8 6.2 4.0 Na₂O 5.0 5.0 5.0 5.0 5.0 5.0 5.0 5.0 3.5 3.5 3.5 3.5 3.5 3.5 3.5 3.5 3.5 3.5 2.7 4.4 K₂O 2.5 2.5 2.5 2.5 2.5 2.5 2.5 2.5 1.8 1.8 1.8 1.8 1.8 1.8 1.8 1.8 1.8 1.8 2.4 2.2 MgO 3.0 2.2 2.0 CaO 3.0 2.2 2.0 SrO 3.0 BaO 3.0 ZnO 3.0 TiO₂ 1.9 0.4 1.9 0.4 1.9 1.9 1.9 1.9 1.9 0.9 0.9 0.9 0.9 0.9 0.9 0.9 0.9 0.9 3.3 3.1 ZrO₂ 0.6 0.4 0.6 0.4 1.0 1.0 1.0 1.0 1.9 0.9 0.9 0.9 0.9 0.9 0.9 0.9 0.9 0.9 4.2 3.9 La₂O₃ 0.7 0.5 0.7 0.5 1.3 1.3 1.3 1.3 2.4 1.4 1.4 1.4 1.4 1.4 1.4 1.4 1.4 1.4 1.6 4.3 CeO₂ Er₂O₃ Gd₂O₃ 3.0 Y₂O₃ 3.0 Nb₂O₅ 2.0 3.0 2.0 3.0 3.0 Ta₂O₅ 3.0 Sb₂O₃ 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 SiO₂ + Al₂O₃ + B₂O₃ 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 75.0 73.9 R₂O:Li₂O + Na₂O + 13.0 14.0 13.0 14.0 14.0 14.0 14.0 14.0 12.0 12.0 12.0 12.0 12.0 12.0 12.0 12.0 12.0 12.0 11.3 10.5 K₂O R′O:MgO + CaO + 3.0 3.0 3.0 3.0 3.0 4.3 4.0 SrO + BaO + ZnO Al₂O₃/B₂O₃ 2.77 2.77 3.57 3.57 3.34 9.68 2.77 3.57 5.18 5.18 5.18 5.18 5.18 5.18 5.18 5.18 5.18 5.18 1.47 1.47 (SiO₂ + Al₂O₃ + B₂O₃)/ 6.24 5.80 6.24 5.80 5.80 5.80 5.80 5.80 6.76 6.76 6.76 6.76 6.76 5.41 5.41 5.41 5.41 5.41 4.81 5.08 (R₂O + R′O) TiO₂ + ZrO₂ + LnxOy 5.2 4.2 5.2 4.2 4.2 4.2 4.2 4.2 6.2 6.2 6.2 6.2 6.2 3.2 3.2 3.2 3.2 3.2 9.1 11.3 Specific Elastic Modulus 33.4 33.6 33.1 33.2 33.5 33.3 33.7 33.4 33.7 33.8 33.7 33.6 33.4 34.0 34.2 33.5 33.4 33.7 34.5 32.9 (E/ρ) Expansion Coefficient 69 72 70 73 72 73 73 72 66 66 67 66 66 65 68 68 68 66 66 66 α(×10⁻⁷/° C.) Vickers Hardness Hv 571 572 557 555 562 578 581 576 580 575 572 582 588 588 586 577 575 589 598 600 Fracture Toughness Kc 1.13 1.05 1.22 1.11 1.21 1.18 1.16 1.22 1.21 1.23 1.20 1.27 1.33 1.10 1.08 1.05 0.99 1.11 0.99 1.05 Alkali Elution A(ppb) 161 200 286 317 201 152 168 221 165 158 177 135 126 211 198 229 244 188 195 257 Tg 503 495 496 487 492 496 493 495 512 509 506 511 512 510 508 502 503 511 510 528 T_(L) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ T_(logη=2) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯

TABLE 5 Practical Example Glass Composition (% by Weight) 81 82 83 84 85 86 87 88 89 90 91 92 93 94 95 96 97 98 99 100 SiO₂ 56.1 53.4 67.6 66.0 66.8 66.8 66.8 68.0 66.8 66.8 68.1 66.8 66.8 66.8 66.8 66.8 66.8 66.8 66.8 69.8 Al₂O₃ 11.6 11.1 9.4 9.2 9.3 9.3 9.3 9.3 10.5 9.3 9.5 9.3 9.3 9.3 9.3 9.3 9.3 9.3 9.3 11.8 B₂O₃ 7.9 7.5 5.4 5.3 5.4 5.4 5.4 5.4 5.4 5.4 3.4 5.4 5.4 5.4 5.4 5.4 5.4 5.4 5.4 3.5 Li₂O 5.7 3.4 5.0 4.9 5.4 5.4 5.0 5.0 5.0 4.5 4.6 4.5 4.5 4.5 4.5 4.5 4.5 4.5 4.5 4.7 Na₂O 2.1 6.2 5.6 5.4 6.0 6.0 5.5 5.5 5.5 7.4 7.6 5.0 5.0 5.0 5.0 5.0 5.0 5.0 5.0 5.2 K₂O 2.1 1.7 2.8 2.7 3.0 3.0 2.8 2.8 2.8 2.5 2.6 2.5 2.5 2.5 2.5 2.5 2.5 2.5 2.5 2.6 MgO 1.9 2.2 CaO 1.9 2.2 SrO BaO ZnO TiO₂ 2.9 3.3 1.9 1.9 1.9 1.9 3.1 1.9 1.9 1.9 2.0 3.8 3.1 1.0 0.4 1.0 0.4 1.0 0.4 2.0 ZrO₂ 3.6 4.2 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.0 3.1 1.0 0.4 1.0 0.4 1.0 0.4 La₂O₃ 4.1 4.6 1.4 1.3 0.5 1.3 0.5 1.3 0.5 CeO₂ Er₂O₃ Gd₂O₃ Y₂O₃ Nb₂O₅ 2.4 3.0 5.0 3.0 5.0 3.0 5.0 Ta₂O₅ Sb₂O₃ 0.2 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 SiO₂ + Al₂O₃ + B₂O₃ 75.5 72.0 82.4 80.4 81.4 81.4 81.4 82.6 82.6 81.4 81.0 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 85.1 R₂O:Li₂O + Na₂O + 9.9 11.3 13.4 13.1 14.5 14.5 13.3 13.3 13.3 14.5 14.8 12.0 12.0 12.0 12.0 12.0 12.0 12.0 12.0 12.6 K₂O R′O:MgO + CaO + 3.8 4.3 SrO + BaO + ZnO Al₂O₃/B₂O₃ 1.47 1.47 1.73 1.73 1.73 1.73 1.73 1.73 1.95 1.73 2.75 1.73 1.73 1.73 1.73 1.73 1.73 1.73 1.73 3.34 (SiO₂ + Al₂O₃ + B₂O₃)/ 5.54 4.62 6.15 6.15 5.63 5.62 6.12 6.21 6.21 5.62 5.48 6.76 6.76 6.76 6.76 6.76 6.76 6.76 6.76 6.76 (R₂O + R′O) TiO₂ + ZrO₂ + LnxOy 10.6 12.1 3.8 6.2 3.8 3.8 5.0 3.8 3.8 3.8 3.9 6.2 6.2 6.2 6.2 6.2 6.2 6.2 6.2 2.0 Specific Elastic Modulus 32.8 32.8 33.5 33.3 33.7 33.5 33.6 33.6 33.5 33.2 33.0 33.2 33.3 32.8 33.1 32.7 32.4 32.8 32.8 33.2 (E/ρ) Expansion Coefficient 65 67 67 66 71 72 68 68 68 70 73 65 65 65 65 64 66 66 66 66 α(×10⁻⁷/° C.) Vickers Hardness Hv 588 616 577 591 585 587 579 587 581 586 570 585 584 577 572 573 561 569 566 568 Fracture Toughness Kc 1.00 0.99 1.02 1.22 1.06 1.06 0.97 1.00 1.08 0.96 0.97 0.96 1.26 1.02 1.06 1.06 1.08 1.07 0.96 1.39 Alkali Elution A(ppb) 158 224 147 161 189 198 167 155 128 221 281 142 135 128 124 172 161 173 173 169 Tg 517 530 502 504 495 494 507 499 505 490 500 510 515 507 510 503 504 512 520 502 T_(L) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ T_(logη=2) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯

TABLE 6 Practical Example Comparative Example Glass Composition (% by Weight) 101 102 103 104 105 106 107 108 109 110 111 112 113 114 115 116 117 118 1 2 3 SiO₂ 67.8 67.8 67.8 67.8 67.8 69.8 66.8 66.8 66.8 66.8 66.8 66.8 66.8 66.8 66.8 66.8 66.8 66.8 43.1 76.8 52.1 Al₂O₃ 11.8 11.8 11.8 11.8 11.8 13.9 11.3 11.3 11.3 13.3 11.3 11.3 11.3 11.3 11.3 11.3 11.3 13.3 5.6 12.3 5.6 B₂O₃ 3.5 3.5 3.5 3.5 3.5 1.4 3.4 3.4 3.4 1.4 3.4 3.4 3.4 3.4 3.4 3.4 3.4 1.4 8.9 3.4 3.9 Li₂O 4.7 4.7 4.7 4.7 4.7 4.7 4.5 4.5 5.7 5.7 4.5 4.5 4.5 4.5 6.5 2.5 6.5 4.5 4.1 2.5 5.2 Na₂O 5.2 5.2 5.2 5.2 5.2 5.2 5.0 5.0 6.2 6.2 5.0 5.0 5.0 5.0 3.0 7.0 5.0 5.0 4.5 2.0 10.7 K₂O 2.6 2.6 2.6 2.6 2.6 2.6 2.5 2.5 3.1 3.1 2.5 2.5 2.5 2.5 2.5 2.5 0.5 2.5 2.3 2.5 9.4 MgO 2.0 7.3 2.0 CaO 2.0 3.0 3.0 3.0 3.0 3.0 3.0 3.0 3.0 6.3 2.0 SrO 2.0 BaO 2.0 ZnO 2.0 TiO₂ 2.0 2.0 2.0 2.0 2.0 2.0 3.8 3.8 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 6.5 3.5 ZrO₂ 1.0 0.6 0.6 0.6 0.6 0.6 0.6 0.6 0.6 0.6 0.6 7.4 4.4 La₂O₃ 2.4 1.4 0.7 0.7 0.7 0.7 0.7 0.7 0.7 3.9 0.4 0.9 CeO₂ Er₂O₃ Gd₂O₃ 0.7 Y₂O₃ 0.7 Nb₂O₅ Ta₂O₅ 0.7 Sb₂O₃ 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 SiO₂ + 83.1 83.1 83.1 83.1 83.1 85.1 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 57.7 92.4 61.7 Al₂O₃ + B₂O₃ R₂O:Li₂O + 12.6 12.6 12.6 12.6 12.6 12.6 12.0 12.0 15.0 15.0 12.0 12.0 12.0 12.0 12.0 12.0 12.0 12.0 10.8 7.0 25.3 Na₂O + K₂O R′O:MgO + 2.0 2.0 2.0 2.0 2.0 3.0 3.0 3.0 3.0 3.0 3.0 3.0 3.0 13.5 0.0 4.0 CaO + SrO + BaO + ZnO Al₂O₃/B₂O₃ 3.34 3.34 3.34 3.34 3.34 9.68 3.34 3.34 3.34 9.68 3.34 3.34 3.34 3.34 3.34 3.34 3.34 9.68 0.63 3.64 1.43 (SiO₂ + 5.70 5.70 5.70 5.70 5.70 6.76 6.76 6.76 5.41 5.41 5.41 5.41 5.41 5.41 5.41 5.41 5.41 5.41 2.37 13.12 2.11 Al₂O₃ + B₂O₃)/ (R₂O + R′O) TiO₂ + 2.0 2.0 2.0 2.0 2.0 2.0 6.2 6.2 3.2 3.2 3.2 3.2 3.2 3.2 3.2 3.2 3.2 3.2 17.7 0.4 8.7 ZrO₂ + LnxOy Specific Elastic 33.8 33.9 32.9 32.9 33.3 32.8 33.0 33.0 33.1 32.9 33.2 33.4 33.5 33.0 34.5 32.9 33.8 33.1 34.7 30.5 30.9 Modulus (E/ρ) Expansion 65 68 68 68 66 67 67 64 74 75 69 68 69 68 70 68 71 69 72 65 98 Coefficient α(×10⁻⁷/° C.) Vickers 577 573 566 559 588 563 569 567 560 562 588 592 574 599 589 578 592 597 688 552 523 Hardness Hv Fracture 1.45 1.30 1.28 1.18 1.38 1.12 1.07 1.32 1.03 1.20 1.08 1.11 1.05 1.03 1.05 1.11 1.06 1.09 0.74 0.92 0.76 Toughness Kc Alkali Elution 188 178 199 202 158 192 176 181 308 307 138 123 142 100 158 112 158 156 388 88 1232 A(ppb) Tg 499 492 490 494 507 494 519 521 492 498 509 511 505 515 500 521 496 512 547 568 456 T_(L) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ X ◯ ◯ T_(logη=2) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ X ◯

TABLE 7 Practical Example Glass Composition (% by Weight) 119 120 121 122 123 124 125 126 127 128 129 130 131 132 133 134 135 136 137 138 SiO₂ 66.8 66.0 65.2 69.0 62.0 66.0 66.0 66.0 69.4 66.8 66.8 66.8 66.8 66.8 66.8 68.1 66.8 66.8 66.8 66.8 Al₂O₃ 9.3 9.2 9.1 7.2 11.2 9.2 9.2 9.2 9.6 9.3 9.3 9.3 9.3 9.3 9.3 9.5 9.3 9.3 9.3 9.3 B₂O₃ 5.4 5.3 5.2 4.3 7.3 5.3 5.3 5.3 5.6 5.4 5.4 5.4 5.4 5.4 5.4 3.4 5.4 5.4 3.4 4.4 Li₂O 4.5 4.9 5.3 4.9 4.9 3.9 4.9 4.9 5.6 5.0 5.0 5.0 5.0 4.0 3.5 5.1 4.0 5.0 5.3 4.5 Na₂O 5.0 5.4 5.9 5.4 5.4 7.2 5.4 5.4 6.2 5.5 5.5 5.5 6.5 7.3 8.1 5.6 5.5 5.5 5.8 5.0 K₂O 2.5 2.7 2.9 2.7 2.7 2.0 2.7 2.7 3.1 2.8 2.8 2.8 1.8 2.0 1.7 2.8 2.8 1.8 2.9 2.5 MgO CaO SrO BaO 1.0 1.0 1.0 ZnO TiO₂ 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 2.0 1.9 1.9 1.9 1.9 ZrO₂ 1.9 1.9 1.8 1.9 1.9 1.9 1.9 1.9 1.9 1.9 3.1 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 La₂O₃ 2.4 2.4 2.4 2.4 2.4 2.4 1.2 1.2 1.2 1.2 1.2 1.2 1.2 2.4 2.4 CeO₂ Er₂O₃ Gd₂O₃ 2.4 Y₂O₃ 2.4 Nb₂O₅ Ta₂O₅ 1.2 Sb₂O₃ 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 SiO₂ + Al₂O₃ + B₂O₃ 81.4 80.4 79.5 80.4 80.4 80.4 80.4 80.4 84.6 81.4 81.4 81.4 81.4 81.4 81.4 81.0 81.4 81.4 79.4 80.4 R₂O:Li₂O + Na₂O + 12.0 13.1 14.1 13.1 13.1 13.1 13.1 13.1 15.0 13.3 13.3 13.3 13.3 13.3 13.3 13.6 12.3 12.3 14.0 12.0 K₂O R′O:MgO + CaO + 1.0 1.0 1.0 SrO + BaO + ZnO Al₂O₃/B₂O₃ 1.73 1.73 1.73 1.66 1.53 1.73 1.73 1.73 1.73 1.73 1.73 1.73 1.73 1.73 1.73 2.75 1.73 1.73 2.75 2.12 TiO₂ + ZrO₂ + LnxOy 6.2 6.2 6.1 6.2 6.2 6.2 6.2 6.2 5.0 5.0 5.0 5.0 5.0 5.0 5.1 5.0 5.0 6.2 6.2 (SiO₂ + Al₂O₃ + B₂O₃)/ 6.76 6.15 5.63 6.15 6.15 6.15 6.15 6.15 5.63 6.12 6.12 6.12 6.12 6.12 6.12 5.97 6.12 6.12 5.66 6.17 (R₂O + R′O) (Al₂O₃ + B₂O₃)/ 0.18 0.18 0.18 0.14 0.23 0.18 0.18 0.18 0.18 0.18 0.18 0.18 0.18 0.18 0.18 0.16 0.18 0.18 0.16 0.17 (SiO₂ + Al₂O₃ + B₂O₃) Specific Elastic Modulus 33.0 32.4 33.2 32.6 32.4 32.4 33.3 33.0 33.5 33.3 33.4 33.5 33.5 32.9 32.9 33.1 32.8 33.3 32.9 32.7 (E/ρ) Expansion Coefficient 65 70 71 70 68 69 69 69 73 68 67 69 69 69 69 70 66 66 72 66 α(×10⁻⁷/° C.) Vickers Hardness Hv 621 595 583 586 603 590 589 586 584 566 571 590 589 595 590 575 581 583 576 587 Fracture Toughness Kc 1.06 1.06 1.05 1.10 1.03 1.03 1.07 1.06 1.08 1.04 1.10 0.96 1.00 1.02 0.98 1.05 1.01 1.00 0.98 1.04 Alkali Elution A (ppb) 159 190 218 165 174 174 156 160 207 165 142 162 165 189 205 225 117 127 278 154 Weight Reduction 5.0 5.5 4.9 3.9 6.7 4.8 4.8 4.8 4.9 4.8 4.8 4.8 4.8 4.8 4.8 3.2 4.8 4.8 4.2 4.0 Factor (%) Tg 511 5.7 498 510 505 511 511 508 480 505 508 502 501 512 515 499 508 506 493 511 T_(L) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ T_(logη=2) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯

TABLE 8 Practical Example Glass Composition (% by Weight) 139 140 141 142 143 144 145 146 147 148 149 150 151 152 153 154 155 156 157 158 SiO₂ 66.8 66.8 66.8 66.8 66.8 66.8 66.8 66.8 66.1 66.8 68.4 64.6 69.1 71.5 62.5 58.2 60.1 67.6 64.4 66.8 Al₂O₃ 9.3 9.3 9.3 9.3 9.3 9.3 9.3 9.3 9.2 9.3 9.5 9.0 9.6 9.9 13.9 18.5 13.5 9.4 8.9 9.3 B₂O₃ 3.4 3.4 5.4 3.4 5.4 5.4 5.4 5.4 5.3 5.4 5.5 5.2 2.7 5.0 4.7 7.8 5.4 5.2 5.4 Li₂O 4.5 6.5 6.5 4.5 4.5 4.5 4.5 6.5 6.5 4.5 4.0 5.2 4.5 4.5 4.5 4.5 4.5 4.1 5.7 3.0 Na₂O 5.0 3.0 3.0 5.0 5.0 5.0 5.0 3.0 2.9 5.0 4.5 5.7 5.0 5.0 5.0 5.0 5.0 4.6 6.3 6.0 K₂O 2.5 2.5 2.5 2.5 2.5 2.5 2.5 2.5 2.5 2.5 2.2 2.9 2.5 2.5 2.5 2.5 2.5 2.3 3.2 3.0 MgO CaO SrO 1.0 0.6 BaO 1.0 1.0 1.2 1.0 1.2 0.6 1.0 1.0 1.0 1.0 ZnO 1.0 1.0 TiO₂ 1.9 1.9 1.9 1.9 1.9 1.9 0.9 1.9 1.9 1.9 1.7 2.2 1.9 1.9 1.9 1.9 1.9 1.9 1.8 1.9 ZrO₂ 1.9 1.9 1.9 1.9 1.9 1.9 1.9 0.9 1.9 0.9 1.7 2.1 1.9 1.9 1.9 1.9 1.9 1.9 1.8 1.9 La₂O₃ 2.4 2.4 1.2 2.4 1.2 1.2 2.4 2.4 2.4 2.4 2.2 2.8 2.4 2.4 2.4 2.4 2.4 2.5 2.4 2.4 CeO₂ Er₂O₃ Gd₂O₃ Y₂O₃ Nb₂O₅ Ta₂O₅ Sb₂O₃ 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.4 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 SiO₂ + Al₂O₃ + B₂O₃ 79.4 79.4 81.4 79.4 81.4 81.4 81.4 81.4 80.6 81.4 83.4 78.8 81.4 81.4 81.4 81.4 81.4 82.4 78.6 81.4 R₂O:Li₂O + Na₂O + 12.0 12.0 12.0 12.0 12.0 12.0 12.0 12.0 11.9 12.0 10.7 13.7 12.0 12.0 12.0 12.0 12.0 11.0 15.1 12.0 K₂O R′O:MgO + CaO + 2.0 2.0 1.2 2.0 1.2 1.2 1.0 1.0 1.0 1.0 SrO + BaO + ZnO Al₂O₃/B₂O₃ 2.75 2.75 1.73 2.75 1.73 1.73 1.73 1.73 1.73 1.73 1.73 1.73 3.57 — 2.77 3.96 1.73 1.73 1.73 1.73 TiO₂ + ZrO₂ + LnxOy 6.2 6.2 5.0 6.2 5.0 5.0 5.2 5.2 6.2 5.2 5.6 7.1 6.2 6.2 6.2 6.2 6.2 6.3 6.0 6.2 (SiO₂ + Al₂O₃ + B₂O₃)/ 5.66 5.66 6.15 5.66 6.15 6.15 6.24 6.24 6.24 6.24 7.78 5.75 6.76 6.76 6.76 6.76 6.76 7.51 5.20 6.76 (R₂O + R′O) (Al₂O₃ + B₂O₃)/ 0.16 0.16 0.18 0.16 0.18 0.18 0.18 0.18 0.18 0.18 0.18 0.18 0.15 0.12 0.23 0.29 0.26 0.18 0.18 0.18 (SiO₂ + Al₂O₃ + B₂O₃) Specific Elastic Modulus 32.6 33.3 33.7 32.6 33.1 33.3 32.7 33.4 33.3 32.9 32.9 33.0 32.8 32.3 32.8 32.5 32.7 32.9 33.3 32.3 (E/ρ) Expansion Coefficient 66 66 65 64 63 65 66 66 66 64 61 70 66 66 66 66 66 62 76 63 α(×10⁻⁷/° C.) Vickers Hardness Hv 580 588 575 578 575 590 583 587 589 582 577 579 557 556 569 570 574 572 577 586 Fracture Toughness Kc 1.03 1.04 0.99 1.09 1.04 1.05 1.03 0.98 1.01 1.03 1.15 0.95 1.11 1.18 1.09 1.12 1.15 1.16 0.93 1.10 Alkali Elution A (ppb) 154 170 156 150 111 127 150 198 168 164 122 242 155 285 154 187 170 148 316 151 Weight Reduction 3.1 3.6 5.0 3.1 4.8 4.8 4.8 5.0 5.1 4.8 4.8 4.9 2.6 0.3 4.5 4.2 7.1 4.8 4.9 4.8 Factor (%) Tg 510 518 513 511 510 506 504 498 510 509 514 505 511 515 515 534 512 514 494 521 T_(L) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ T_(logη=2) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯

TABLE 9 Practical Example Glass Composition (% by Weight) 159 160 161 162 163 164 165 166 167 168 169 170 171 172 173 174 175 176 177 178 SiO₂ 66.8 66.8 66.8 66.8 66.8 66.8 66.8 66.1 64.8 66.1 66.1 64.8 66.1 66.1 64.8 66.1 64.8 64.8 64.8 64.8 Al₂O₃ 9.3 9.3 9.3 9.3 9.3 9.3 9.3 9.2 9.0 9.2 9.2 9.0 9.2 9.2 9.0 9.2 9.0 9.0 9.0 9.0 B₂O₃ 5.4 5.4 5.4 5.4 5.4 5.4 5.4 5.3 5.2 5.3 5.3 5.2 5.3 5.3 5.2 5.3 5.2 5.2 5.2 5.2 Li₂O 1.5 2.9 1.3 3.9 3.3 4.9 5.3 4.5 4.4 6.5 4.5 4.4 5.5 4.5 4.4 4.5 4.4 4.4 4.4 4.4 Na₂O 7.0 7.5 10.0 4.3 3.7 5.4 5.9 4.9 4.9 2.9 4.9 4.9 3.9 4.9 4.9 4.9 4.9 4.9 4.9 4.9 K₂O 3.5 1.6 0.7 3.8 5.0 1.7 0.8 2.5 2.4 2.5 2.5 2.4 2.5 2.5 2.4 2.5 2.4 2.4 2.4 2.4 MgO 1.0 1.0 2.9 CaO 1.0 2.9 2.9 2.9 2.9 SrO 1.0 1.0 2.9 BaO 1.0 2.9 ZnO TiO₂ 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 ZrO₂ 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.8 1.9 1.9 1.8 1.9 1.9 1.8 1.9 1.8 1.8 1.8 1.8 La₂O₃ 2.4 2.4 2.4 2.4 2.4 2.4 2.4 2.4 2.4 2.4 2.4 2.4 2.4 2.4 2.4 2.4 2.4 CeO₂ Er₂O₃ Gd₂O₃ 2.4 Y₂O₃ 2.4 Nb₂O₅ 2.4 Ta₂O₅ Sb₂O₃ 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 SiO₂ + Al₂O₃ + B₂O₃ 81.4 81.4 81.4 81.4 81.4 81.4 81.4 80.6 79.0 80.6 80.6 79.0 80.6 80.6 79.0 80.6 79.0 79.0 79.0 79.0 R₂O:Li₂O + Na₂O + 12.0 12.0 12.0 12.0 12.0 12.0 12.0 11.9 11.7 11.9 11.9 11.7 11.9 11.9 11.7 11.9 11.7 11.7 11.7 11.7 K₂O R′O:MgO + CaO + 1.0 2.9 1.0 1.0 2.9 1.0 1.0 2.9 1.0 2.9 2.9 2.9 2.9 SrO + BaO + ZnO Al₂O₃/B₂O₃ 1.73 1.73 1.73 1.73 1.73 1.73 1.73 1.73 1.73 1.73 1.73 1.73 1.73 1.73 1.73 1.73 1.73 1.73 1.73 1.73 TiO₂ + ZrO₂ + LnxOy 6.2 6.2 6.2 6.2 6.2 6.2 6.2 6.2 6.0 6.2 6.2 6.0 6.2 6.2 6.0 6.2 6.0 6.0 6.0 6.0 (SiO₂ + Al₂O₃ + B₂O₃)/ 6.76 6.76 6.76 6.76 6.76 6.76 6.76 6.24 5.41 6.24 6.24 5.41 6.24 6.24 5.41 6.24 5.41 5.41 5.41 5.41 (R₂O + R′O) (Al₂O₃ + B₂O₃)/ 0.18 0.18 0.18 0.18 0.18 0.18 0.18 0.18 0.18 0.18 0.18 0.18 0.18 0.18 0.18 0.18 0.18 0.18 0.18 0.18 (SiO₂ + Al₂O₃ + B₂O₃) Specific Elastic Modulus 31.5 32.3 31.5 32.6 32.1 33.1 33.6 32.8 32.5 34.1 32.9 32.7 33.4 32.9 33.3 33.1 33.4 33.5 33.8 33.4 (E/ρ) Expansion Coefficient 64 65 65 62 63 66 67 64 66 67 64 67 65 64 65 66 67 66 67 65 α(×10⁻⁷/° C.) Vickers Hardness Hv 571 575 565 563 561 578 585 584 581 588 581 566 575 574 587 573 586 588 577 588 Fracture Toughness Kc 1.07 1.08 1.11 1.14 1.28 1.04 0.96 1.05 0.96 1.03 1.06 1.05 1.02 1.09 1.05 1.00 1.01 1.01 0.99 1.03 Alkali Elution A (ppb) 157 172 258 134 130 216 204 168 129 269 228 157 142 142 139 168 174 152 166 135 Weight Reduction 3.9 4.8 4.8 4.8 4.8 4.8 4.8 4.8 4.8 5.0 4.8 4.8 5.0 4.8 4.8 4.8 4.8 4.6 4.9 4.7 Factor (%) Tg 546 524 544 513 526 511 510 518 511 504 510 509 510 508 512 512 512 515 509 513 T_(L) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ T_(logη=2) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯

TABLE 10 Practical Example Glass Composition (% by Weight) 179 180 181 182 183 184 185 186 187 188 189 190 191 192 193 194 195 196 197 198 SiO₂ 64.8 66.1 64.8 66.1 64.8 66.8 66.8 66.8 66.8 66.8 66.8 66.8 66.8 66.8 66.8 66.8 66.8 60.5 66.9 64.6 Al₂O₃ 9.0 12.2 12.0 9.2 9.0 9.3 9.3 9.3 9.3 9.3 9.3 9.3 9.3 9.3 9.3 9.3 9.3 13.5 9.3 12.0 B₂O₃ 5.2 2.3 2.2 5.3 5.2 2.4 2.4 2.4 2.4 5.4 5.4 5.4 5.4 5.4 5.4 5.4 5.4 4.9 2.6 2.2 Li₂O 4.4 4.5 4.4 4.5 4.4 4.5 4.5 4.5 4.5 4.5 4.5 4.5 4.5 4.5 4.5 4.5 4.5 5.2 5.2 5.2 Na₂O 4.9 4.9 4.9 4.9 4.9 5.0 5.0 5.0 5.0 5.0 5.0 5.0 5.0 5.0 5.0 5.0 5.0 5.7 5.7 5.7 K₂O 2.4 2.5 2.4 2.5 2.4 2.5 2.5 2.5 2.5 2.5 2.5 2.5 2.5 2.5 2.5 2.5 2.5 2.9 2.9 2.9 MgO 3.0 5.0 CaO 2.9 3.0 3.0 5.0 SrO 3.0 3.0 5.0 BaO 3.0 3.0 5.0 ZnO 1.0 2.9 1.0 2.9 3.0 TiO₂ 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.0 1.0 1.0 1.0 0.4 0.4 0.4 0.4 2.2 2.2 2.2 ZrO₂ 1.8 1.9 1.8 1.9 1.8 1.9 1.9 1.9 1.9 1.0 1.0 1.0 1.0 0.4 0.4 0.4 0.4 2.1 2.1 2.1 La₂O₃ 2.4 2.4 2.4 2.4 2.4 2.4 2.4 2.4 1.3 1.3 1.3 1.3 0.5 0.5 0.5 0.5 2.8 2.8 2.8 CeO₂ Er₂O₃ Gd₂O₃ Y₂O₃ Nb₂O₅ Ta₂O₅ 2.4 Sb₂O₃ 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.4 0.4 0.4 SiO₂ + Al₂O₃ + B₂O₃ 79.0 80.6 79.0 80.6 79.0 78.4 78.4 78.4 78.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 81.4 78.8 78.8 78.8 R₂O:Li₂O + Na₂O + 11.7 11.9 11.7 11.9 11.7 12.0 12.0 12.0 12.0 12.0 12.0 12.0 12.0 12.0 12.0 12.0 12.0 13.7 13.7 13.7 K₂O R′O:MgO + CaO + 2.9 1.0 2.9 1.0 2.9 3.0 3.0 3.0 3.0 3.0 3.0 3.0 3.0 5.0 5.0 5.0 5.0 SrO + BaO + ZnO Al₂O₃/B₂O₃ 1.73 5.25 5.42 1.73 1.73 3.91 3.91 3.91 3.91 1.73 1.73 1.73 1.73 1.73 1.73 1.73 1.73 2.77 3.57 5.44 TiO₂ + ZrO₂ + LnxOy 6.0 6.2 6.0 6.2 6.0 6.2 6.2 6.2 6.2 3.2 3.2 3.2 3.2 1.2 1.2 1.2 1.2 7.1 7.1 7.1 (SiO₂ + Al₂O₃ + B₂O₃)/ 5.41 6.24 5.41 6.24 5.41 5.21 5.21 5.21 5.21 5.41 5.41 5.41 5.41 4.78 4.78 4.78 4.78 5.75 5.75 5.75 (R₂O + R′O) (Al₂O₃ + B₂O₃)/ 0.18 0.18 0.18 0.18 0.18 0.15 0.15 0.15 0.15 0.18 0.18 0.18 0.18 0.18 0.18 0.18 0.18 0.23 0.15 0.18 (SiO₂ + Al₂O₃ + B₂O₃) Specific Elastic Modulus 33.4 33.6 33.1 32.9 32.2 32.2 32.5 32.9 32.3 32.7 33.0 33.4 33.4 32.2 32.5 33.6 33.7 33.0 32.7 32.8 (E/ρ) Expansion Coefficient 65 67 66 64 63 67 68 69 67 66 67 67 65 68 69 68 66 71 72 70 α(×10⁻⁷/° C.) Vickers Hardness Hv 592 578 590 576 581 580 572 583 570 580 584 576 572 561 572 585 581 576 583 586 Fracture Toughness Kc 1.05 1.21 1.25 1.06 1.00 1.05 1.10 1.04 1.12 1.06 1.06 1.02 1.14 1.01 0.95 0.97 1.04 1.08 0.98 1.07 Alkali Elution A (ppb) 110 199 154 177 135 207 259 166 208 210 172 168 128 151 143 153 131 230 275 273 Weight Reduction 4.3 2.8 2.4 4.8 4.8 2.3 2.3 2.3 2.3 4.8 4.8 4.8 4.8 4.8 4.8 4.8 4.8 4.5 2.5 2.2 Factor (%) Tg 515 518 511 509 504 505 506 519 504 505 500 505 500 496 498 505 505 502 508 512 T_(L) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ T_(logη=2) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯

TABLE 11 Practical Example Glass Composition (% by Weight) 199 200 201 202 203 204 205 206 207 208 SiO₂ 66.8 66.8 66.8 66.8 68.9 71.2 62.8 64.6 65.2 61.0 Al₂O₃ 9.3 9.3 9.3 9.3 9.6 9.9 8.7 9.0 9.1 13.6 B₂O₃ 5.4 5.4 5.4 5.4 5.5 5.7 5.1 5.2 5.2 4.9 Li₂O 4.5 4.5 4.5 4.5 4.7 4.8 4.3 3.3 5.9 5.3 Na₂O 5.0 5.0 5.0 5.0 5.2 5.3 4.7 8.5 5.3 5.9 K₂O 2.5 2.5 2.5 2.5 2.6 2.7 2.4 1.8 2.9 2.9 MgO CaO SrO BaO ZnO TiO₂ 2.7 1.1 0.7 1.0 3.6 2.2 1.9 1.9 ZrO₂ 2.7 3.7 0.7 1.0 3.5 2.1 1.8 1.8 La₂O₃ 3.5 3.5 1.4 4.9 1.3 4.6 2.8 2.4 2.4 CeO₂ Er₂O₃ Gd₂O₃ Y₂O₃ Nb₂O₅ Ta₂O₅ Sb₂O₃ 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.4 0.3 0.3 SiO₂ + Ai₂O₃ + B₂O₃ 81.4 81.4 81.4 81.4 84.0 86.8 76.6 78.8 79.5 79.5 R₂O:Li₂O + Na₂O + K₂O 12.0 12.0 12.0 12.0 12.4 12.8 11.3 13.7 14.1 14.1 R′O:MgO + CaO + SrO + BaO + ZnO Al₂O₃/B₂O₃ 1.73 1.73 1.73 1.73 1.73 1.73 1.73 1.73 1.73 2.77 TiO₂ + ZrO₂ + LnxOy 6.2 6.2 6.2 6.2 3.2 11.7 7.1 6.1 6.1 (SiO₂ + Al₂O₃ + B₂O₃)/(R₂O + R′O) 6.76 6.76 6.76 6.76 6.76 6.76 6.76 5.75 5.63 5.63 (Al₂O₃ + B₂O₃)/(SiO₂ + Al₂O₃ + B₂O₃) 0.18 0.18 0.18 0.18 0.18 0.18 0.18 0.18 0.18 0.23 Specific Elastic Modulus (E/ρ) 32.9 32.9 33.1 32.6 33.2 33.4 32.7 32.6 33.7 33.0 Expansion Coefficient α (×10⁻⁷/° C.) 65 65 64 66 65 65 65 67 71 68 Vickers Hardness Hv 584 583 585 581 573 568 605 580 585 578 Fracture Toughness Kc 1.24 0.95 1.04 1.07 1.23 1.15 1.03 0.94 1.09 0.98 Alkali Elution A (ppb) 163 147 140 192 145 93 171 297 197 258 Weight Reduction Factor (%) 4.8 4.8 4.8 4.8 4.8 4.8 4.8 4.9 4.8 4.5 Tg 511 512 514 506 497 493 525 513 503 505 T_(L) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ T_(log η=2) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ Pratical Example Glass Composition (% by Weight) 209 210 211 212 213 214 215 216 217 218 SiO₂ 67.5 65.2 65.2 67.1 60.7 65.0 61.7 68.3 66.0 66.0 Al₂O₃ 9.4 11.1 13.1 9.3 13.5 10.2 13.7 9.5 11.2 13.2 B₂O₃ 2.6 3.2 1.2 2.6 4.9 5.3 5.0 2.7 3.3 1.3 Li₂O 5.3 5.3 5.3 4.4 4.4 4.9 4.9 4.9 4.9 4.9 Na₂O 5.9 5.9 5.9 4.9 4.9 5.4 5.4 5.4 5.4 5.4 K₂O 2.9 2.9 2.9 2.4 2.4 2.7 2.7 2.7 2.7 2.7 MgO CaO 2.9 2.9 SrO BaO ZnO TiO₂ 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 1.9 ZrO₂ 1.8 1.8 1.8 1.8 1.8 1.9 1.9 1.9 1.9 1.9 La₂O₃ 2.4 2.4 2.4 2.4 2.4 2.4 2.4 2.4 2.4 2.4 CeO₂ Er₂O₃ Gd₂O₃ Y₂O₃ Nb₂O₅ Ta₂O₅ Sb₂O₃ 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 SiO₂ + Ai₂O₃ + B₂O₃ 79.5 79.5 79.5 79.0 79.0 80.4 80.4 80.4 80.4 80.4 R₂O:Li₂O + Na₂O + K₂O 14.1 14.1 14.1 11.7 11.7 13.1 13.1 13.1 13.1 13.1 R′O:MgO + CaO + SrO + BaO + ZnO 2.9 2.9 Al₂O₃/B₂O₃ 3.57 3.41 10.49 3.57 2.77 1.73 2.77 3.57 3.37 10.07 TiO₂ + ZrO₂ + LnxOy 6.1 6.1 6.1 6.0 6.0 6.2 6.2 6.2 6.2 6.2 (SiO₂ + Al₂O₃ + B₂O₃)/(R₂O + R′O) 5.63 5.63 5.63 5.41 5.41 6.15 6.15 6.15 6.15 6.15 (Al₂O₃ + B₂O₃)/(SiO₂ + Al₂O₃ + B₂O₃) 0.15 0.18 0.18 0.15 0.23 0.18 0.23 0.15 0.18 0.18 Specific Elastic Modulus (E/ρ) 32.7 33.0 32.8 32.9 33.2 33.0 33.0 32.9 33.0 32.8 Expansion Coefficient α (×10⁻⁷/° C.) 68 73 77 68 68 68 69 69 71 72 Vickers Hardness Hv 569 576 566 576 596 585 577 563 581 566 Fracture Toughness Kc 1.05 1.04 1.12 1.06 1.03 1.10 1.13 1.13 1.13 1.14 Alkali Elution A (ppb) 334 238 259 132 102 221 170 248 198 221 Weight Reduction Factor (%) 2.5 3.1 1.4 2.5 4.5 4.9 4.5 2.5 3.1 1.4 Tg 497 497 507 512 519 499 507 502 506 510 T_(L) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ T_(log η=2) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯

TABLE 12 Practical Example Glass Composition (% by Weight) 219 220 221 222 223 224 225 226 SiO₂ 61.7 68.3 66.0 66.0 66.8 68.2 68.2 66.8 Al₂O₃ 13.7 9.5 11.2 13.2 9.3 11.5 13.6 11.3 B₂O₃ 5.0 2.7 3.3 1.3 5.4 3.4 1.4 3.4 Li₂O 4.9 4.9 4.9 4.9 5.5 4.6 4.6 5.3 Na₂O 5.4 5.4 5.4 5.4 2.5 5.1 5.1 5.8 K₂O 2.7 2.7 2.7 2.7 4.0 2.6 2.6 2.9 MgO CaO SrO BaO ZnO TiO₂ 1.9 1.9 1.9 1.9 1.9 2.0 2.0 1.9 ZrO₂ 1.9 1.9 1.9 1.9 1.9 1.0 1.0 1.0 La₂O₃ 2.4 2.4 2.4 2.4 2.4 1.2 1.2 1.3 CeO₂ Er₂O₃ Gd₂O₃ Y₂O₃ Nb₂O₅ Ta₂O₅ Sb₂O₃ 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 SiO₂ + Al₂O₃ + B₂O₃ 80.4 80.4 80.4 80.4 81.4 83.2 83.2 81.4 R₂O:Li₂O + Na₂O + K₂O 13.1 13.1 13.1 13.1 12.0 12.3 12.3 14.0 R′O:MgO + CaO + SrO + BaO + ZnO Al₂O₃/B₂O₃ 2.77 3.57 3.37 10.07 1.73 3.34 9.68 3.34 TiO₂ + ZrO₂ + LnxOy 6.2 6.2 6.2 6.2 6.2 4.2 4.2 4.2 (SiO₂ + Al₂O₃ + B₂O₃)/(R₂O + R′O) 6.15 6.15 6.15 6.15 6.76 6.76 6.76 5.80 (Al₂O₃ + B₂O₃)/(SiO₂ + Al₂O₃ + B₂O₃) 0.23 0.15 0.18 0.18 0.18 0.18 0.18 0.18 Specific Elastic Modulus (E/ρ) 33.4 33.3 33.3 33.1 33.3 32.9 32.7 32.9 Expansion Coefficient α (×10⁻⁷/° C.) 73 73 71 72 66 64 68 72 Vickers Hardness Hv 580 560 564 564 587 568 568 569 Fracture Toughness Kc 1.06 1.33 1.18 1.16 1.01 1.49 1.40 1.13 Alkali Elution A (ppb) 195 248 315 287 118 170 173 257 Weight Reduction Factor (%) 4.5 2.5 3.1 1.4 4.9 3.0 1.4 3.1 Tg 495 495 494 503 506 511 513 499 T_(L) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ T_(log η=2) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ Pratical Example Comparative Ex. Glass Composition (% by Weight) 227 228 229 230 231 232 233 4 5 SiO₂ 66.8 62.5 69.1 66.8 65.2 51.0 53.5 52.0 62.5 Al₂O₃ 13.3 13.9 9.6 12.3 12.1 14.2 14.1 13.6 3.1 B₂O₃ 1.4 5.0 2.7 2.4 2.2 3.6 3.5 15.7 5.8 Li₂O 5.3 5.3 5.3 6.8 5.3 3.7 4.0 4.5 8.5 Na₂O 5.8 5.8 5.8 3.5 5.9 4.1 4.4 5.0 5.0 K₂O 2.9 2.9 2.9 1.8 2.9 2.0 2.2 2.5 2.5 MgO 3.9 5.8 3.0 CaO 5.7 0.7 4.0 SrO BaO ZnO TiO₂ 1.9 1.9 1.9 1.9 1.9 3.2 3.2 1.9 1.9 ZrO₂ 1.0 1.0 1.0 1.9 1.8 4.0 3.9 1.9 1.9 La₂O₃ 1.3 1.3 1.3 2.4 2.4 4.4 4.4 2.4 2.4 CeO₂ Er₂O₃ Gd₂O₃ Y₂O₃ Nb₂O₅ Ta₂O₅ Sb₂O₃ 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 SiO₂ + Al₂O₃ + B₂O₃ 81.4 81.4 81.4 81.4 79.5 68.8 71.1 81.4 71.4 R₂O:Li₂O + Na₂O + K₂O 14.0 14.0 14.0 12.0 14.1 9.8 10.7 12.0 15.0 R′O:MgO + CaO + SrO + BaO + ZnO 9.6 6.5 0.0 7.0 Al₂O₃/B₂O₃ 9.68 2.77 3.57 5.18 5.37 3.99 3.99 0.86 0.53 TiO₂ + ZrO₂ + LnxOy 4.2 4.2 4.2 6.2 6.1 11.6 11.5 6.2 6.2 (SiO₂ + Al₂O₃ + B₂O₃)/(R₂O + R′O) 5.80 5.80 5.80 6.76 5.63 3.55 4.14 6.76 3.24 (Al₂O₃ + B₂O₃)/(SiO₂ + Al₂O₃ + B₂O₃) 0.18 0.23 0.15 0.18 0.18 0.26 0.25 0.36 0.11 Specific Elastic Modulus (E/ρ) 32.9 33.2 32.9 33.7 32.7 34.0 33.5 33.3 34.3 Expansion Coefficient α (×10⁻⁷/° C.) 72 72 72 66 73 72 68 58 79 Vickers Hardness Hv 561 573 569 580 570 664 652 577 558 Fracture Toughness Kc 1.19 1.13 1.11 1.21 1.14 0.90 1.04 0.85 0.79 Alkali Elution A (ppb) 278 152 236 165 240 305 235 420 502 Weight Reduction Factor (%) 1.4 4.5 2.5 2.2 2.2 3.8 3.6 14.7 9.2 Tg 505 499 490 512 502 554 521 538 488 T_(L) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ T_(log η=2) ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ ◯ 

1. A glass composition comprising the following glass ingredients: 45 to 75% by weight of SiO₂; 10.1 to 14.6% by weight of Al₂O₃; 1.2 to 5.7% by weight of B₂O₃; SiO₂+Al₂O₃+B₂O₃ accounting for 65 to 90% by weight; a total of 7 to 12.8% by weight of R₂O compounds, where R=Li, Na, and K; and a total of 0% by weight of R′O compounds, where R′=Mg, Ca, Sr, Ba, and Zn; and a total of 0 to 7.1% by weight, zero inclusive, of TiO₂+ZrO₂+Ln_(x)O_(y), where Ln_(x)O_(y) represents at least one compound selected from the group consisting of lanthanoid metal oxides, Y₂O₃, Nb₂O₅ and Ta₂O₅, wherein the following conditions are fulfilled: Al₂O₃/B₂O₃≧1.0; and 7.78≧(SiO₂+Al₂O₃+B₂O₃)/(the total of R₂O compounds ≧3.
 2. A glass composition as claimed in claim 1, wherein the glass composition has a glass transition temperature Tg of 600° C. or lower.
 3. A glass composition as claimed in claim 1, wherein the glass composition has a liquid phase temperature T_(L) of 1 300° C. or lower.
 4. A glass composition as claimed in claim 1, wherein a temperature T _(log η)=2 at which the glass composition has a melt viscosity of log η=2 is 1 550° C. or lower.
 5. A glass substrate formed of a glass composition comprising the following glass ingredients: 45 to 75% by weight of SiO₂; 10.1 to 14.6% by weight of Al₂O₃; 1.2 to 5.7% by weight of B₂O₃; SiO₂+Al₂O₃+B₂O₃ accounting for 72 to 90% by weight; a total of 7 to 12.8% by weight of R₂O compounds, where R=Li, Na, and K; a total of 0% by weight of R′O compounds, where R′=Mg, Ca, Sr, Ba, and Zn; and a total of 0% to 7.1% by weight, zero inclusive, of TiO₂+ZrO₂+Ln_(x)O_(y), where Ln_(x)O_(y) represents at least one compound selected from the group consisting of lanthanoid metal oxides, Y₂O₃, Nb₂O₅ and Ta₂O₅, wherein the following conditions are fulfilled: Al₂O₃/B₂O₃≧1.0; and 7.78≧(SiO₂+Al₂O₃+B₂O₃)/(the total of R₂O compounds≧3.
 6. A glass substrate as claimed in claim 5, wherein the glass composition has a glass transition temperature Tg of 600° C. or lower.
 7. A glass substrate as claimed in claim 5, wherein the glass composition has a liquid phase temperature T_(L) of 1 300° C. or lower.
 8. A glass substrate as claimed in claim 5, wherein a temperature T_(log η=2) at which the glass composition has a melt viscosity of log η=2 is 1 550° C. or lower.
 9. A glass substrate as claimed in claim 5, wherein the glass substrate is not subjected to chemical strengthening.
 10. A glass substrate as claimed in claim 9, wherein the glass substrate has a specific elastic modulus E/ρ of 31 or higher.
 11. A glass substrate as claimed in claim 9, wherein the glass substrate has a Vickers hardness Hv in a range of from 500 to 700 as measured at a load of 100g.
 12. A glass substrate as claimed in claim 9, wherein the glass substrate has alkali elution A of 350 ppb or lower per 2.5-inch disk.
 13. A glass substrate as claimed in claim 9, wherein the glass substrate has a linear thermal expansion coefficient in a range of from 60×10^(—) ⁷ /° C. to 90 10^(—) ⁷ /° C. within a temperature range of 25 to 100° C.
 14. A glass substrate as claimed in claim 9, wherein the glass substrate has a fracture toughness Kc of 0.80 or greater. 